JP6830951B2 - Optical glass - Google Patents
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- JP6830951B2 JP6830951B2 JP2018506877A JP2018506877A JP6830951B2 JP 6830951 B2 JP6830951 B2 JP 6830951B2 JP 2018506877 A JP2018506877 A JP 2018506877A JP 2018506877 A JP2018506877 A JP 2018506877A JP 6830951 B2 JP6830951 B2 JP 6830951B2
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- 239000005304 optical glass Substances 0.000 title claims description 55
- 239000011521 glass Substances 0.000 claims description 123
- 230000003287 optical effect Effects 0.000 claims description 46
- 229910021193 La 2 O 3 Inorganic materials 0.000 claims description 29
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 27
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 18
- 239000000463 material Substances 0.000 claims description 15
- 229910006404 SnO 2 Inorganic materials 0.000 claims description 9
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 6
- 229910015902 Bi 2 O 3 Inorganic materials 0.000 claims description 6
- 229910005793 GeO 2 Inorganic materials 0.000 claims description 5
- 229910018068 Li 2 O Inorganic materials 0.000 claims description 3
- 229910052708 sodium Inorganic materials 0.000 claims description 3
- 229910052688 Gadolinium Inorganic materials 0.000 claims description 2
- 229910052769 Ytterbium Inorganic materials 0.000 claims description 2
- 229910052715 tantalum Inorganic materials 0.000 claims description 2
- 239000006185 dispersion Substances 0.000 description 27
- 238000002834 transmittance Methods 0.000 description 16
- 239000002585 base Substances 0.000 description 12
- 238000004040 coloring Methods 0.000 description 11
- 238000004031 devitrification Methods 0.000 description 11
- 230000007704 transition Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 7
- 238000000465 moulding Methods 0.000 description 7
- 239000002994 raw material Substances 0.000 description 7
- 239000000126 substance Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 230000005499 meniscus Effects 0.000 description 6
- 238000000034 method Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 5
- 230000003595 spectral effect Effects 0.000 description 5
- 239000002253 acid Substances 0.000 description 4
- 238000002386 leaching Methods 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 239000006060 molten glass Substances 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Substances [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 3
- 238000004017 vitrification Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 150000001450 anions Chemical class 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000000691 measurement method Methods 0.000 description 2
- 150000002823 nitrates Chemical class 0.000 description 2
- 229910052697 platinum Inorganic materials 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 229910001404 rare earth metal oxide Inorganic materials 0.000 description 2
- 150000003467 sulfuric acid derivatives Chemical class 0.000 description 2
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 1
- 229910017768 LaF 3 Inorganic materials 0.000 description 1
- 229910002651 NO3 Inorganic materials 0.000 description 1
- NHNBFGGVMKEFGY-UHFFFAOYSA-N Nitrate Chemical compound [O-][N+]([O-])=O NHNBFGGVMKEFGY-UHFFFAOYSA-N 0.000 description 1
- QAOWNCQODCNURD-UHFFFAOYSA-L Sulfate Chemical compound [O-]S([O-])(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-L 0.000 description 1
- 150000007513 acids Chemical class 0.000 description 1
- 229910001515 alkali metal fluoride Inorganic materials 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- KGBXLFKZBHKPEV-UHFFFAOYSA-N boric acid Chemical compound OB(O)O KGBXLFKZBHKPEV-UHFFFAOYSA-N 0.000 description 1
- 239000004327 boric acid Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 230000009477 glass transition Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000004679 hydroxides Chemical class 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 230000001404 mediated effect Effects 0.000 description 1
- 229910001512 metal fluoride Inorganic materials 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000006082 mold release agent Substances 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- -1 platinum ions Chemical class 0.000 description 1
- 230000011514 reflex Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/062—Glass compositions containing silica with less than 40% silica by weight
- C03C3/064—Glass compositions containing silica with less than 40% silica by weight containing boron
- C03C3/068—Glass compositions containing silica with less than 40% silica by weight containing boron containing rare earths
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/12—Silica-free oxide glass compositions
- C03C3/14—Silica-free oxide glass compositions containing boron
- C03C3/15—Silica-free oxide glass compositions containing boron containing rare earths
- C03C3/155—Silica-free oxide glass compositions containing boron containing rare earths containing zirconium, titanium, tantalum or niobium
Landscapes
- Chemical & Material Sciences (AREA)
- Life Sciences & Earth Sciences (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Glass Compositions (AREA)
Description
本発明は、高屈折低分散光学ガラスに関する。特に、低コストの高屈折低分散光学ガラスと光学素子に関する。 The present invention relates to high refraction low dispersion optical glass. In particular, the present invention relates to low-cost, high-refraction, low-dispersion optical glass and optical elements.
高屈折率低分散光学ガラスからなるレンズと高屈折率高分散光学ガラスからなるレンズを組み合わして、色差を補正することが出来、光学システムがコンパクト化になり、特に屈折率ｎｄが１．８６−１．９２で、アッベ数νｄが３６−４２の高屈折率低分散光学ガラスの市場ニーズが日々増大していく。 By combining a lens made of high-refractive-index low-dispersion optical glass and a lens made of high-refractive-index high-dispersion optical glass, color differences can be corrected, making the optical system compact, and in particular, the refractive index nd is 1.86. At -1.92, the market needs for high refractive index low dispersion optical glass with an Abbe number νd of 36-42 are increasing day by day.
日本特開２００１−３４８２４４、特開２００７−２６９５８４、中国ＣＮ１０１３８６４６９Ａでは、全てこれら高折射低分散光学ガラスを開示しており、その明細書実施例では、屈折率が１．８６以上の光学ガラス成分には大量のＴａ２Ｏ５が含まれており、Ｔａ２Ｏ５は高価な希土類酸化物である。従って、高屈折率低分散光学ガラス原料原価の増加を抑えるために、Ｔａ２Ｏ５含有量を減少して欲しいのだ。また、撮影或いは投射等光学システムの光学素子は、光学ガラスの透過率に対する要求が高く、高折射低分散光学ガラスで出来たレンズから透過する明るさが足りないと、光学システムの投射光度が大幅に低減するか極端に減少してしまうので、優れた透過率性能の光学ガラスを望んでいる。 Japanese Patent Application Laid-Open No. 2001-348244, Japanese Patent Application Laid-Open No. 2007-269584, and China CN1013864669A all disclose these high-folding low-dispersion optical glasses, and in the examples of the specification, the optical glass component having a refractive index of 1.86 or more Contains a large amount of Ta 2 O 5 and Ta 2 O 5 is an expensive rare earth oxide. Therefore, in order to suppress the increase in the cost of raw materials for high-refractive-index, low-dispersion optical glass, we would like you to reduce the Ta 2 O 5 content. In addition, the optical elements of optical systems such as photography or projection have high requirements for the transmittance of optical glass, and if the brightness transmitted from a lens made of high-folding low-dispersion optical glass is insufficient, the projected light intensity of the optical system will be large. I want an optical glass with excellent transmittance performance because it will be reduced or extremely reduced.
本発明が解決しようとする課題は、屈折率が１．８５以上で、アッベ数が３５−４５の高屈折低分散光学ガラスを提供することにある。当該ガラスはＰｂＯを含まず、ガラス成分のＴａ２Ｏ５含有量が低減される場合に優れた透過率を有する。 An object to be solved by the present invention is to provide a high refraction low dispersion optical glass having a refractive index of 1.85 or more and an Abbe number of 35 to 45. The glass does not contain PbO and has excellent transmittance when the Ta 2 O 5 content of the glass component is reduced.
上記課題を解決する目的で、本発明は更に上記光学ガラスからなる光学母材と光学素子を提供する。 For the purpose of solving the above problems, the present invention further provides an optical base material and an optical element made of the above optical glass.
本発明は、重量百分率における、Ｂ２Ｏ３：１−３０％、ＳｉＯ２：０−２０％、Ｌａ２Ｏ３：２５−５５％、Ｇｄ２Ｏ３：５−４０％、Ｙ２Ｏ３：０−２５％、Ｙｂ２Ｏ３：０−１０％、Ｔａ２Ｏ５：０−１０％、Ｎｂ２Ｏ５：１−３０％、ＴｉＯ２：０−１０％、ＴｉＯ２／Ｎｂ２Ｏ５は０．３以下、ＺｒＯ２：０．５−２０％、ＷＯ３：０−１０％、ＺｎＯ：０−１５％；（ＺｎＯ＋Ｙ２Ｏ３）／Ｌａ２Ｏ３の範囲は０．５以下、Ｒ２Ｏ：０−１０％［その内、Ｒ２ＯはＬｉ２Ｏ、Ｎａ２Ｏ或いはＫ２Ｏの１種或いは数種］、ＲＯ：０−１０％［その内、ＲＯはＢａＯ、ＳｒＯ、ＭｇＯ或いはＣａＯの１種或いは数種］、Ａｌ２Ｏ３：０−１０％、ＧｅＯ２：０−１０％、Ｂｉ２Ｏ３：０−１０％を含有する光学ガラスであって、ＰｂＯを含有せず、屈折率の範囲は１．８５以上で、アッベ数の範囲は３５−４５である、該ガラスを提供する。 The present invention relates to B 2 O 3 : 1-30%, SiO 2 : 0-20%, La 2 O 3 : 25-55%, Gd 2 O 3 : 5-40%, Y 2 O 3 in weight percentage. : 0-25%, Yb 2 O 3 : 0-10%, Ta 2 O 5 : 0-10%, Nb 2 O 5 : 1-30%, TiO 2 : 0-10%, TiO 2 / Nb 2 O 5 is 0.3 or less, ZrO 2 : 0.5-20%, WO 3 : 0-10%, ZnO: 0-15%; (ZnO + Y 2 O 3 ) / La 2 O 3 is 0.5 or less. , R 2 O: 0-10% [of which R 2 O is one or several of Li 2 O, Na 2 O or K 2 O], RO: 0-10% [of which RO is BaO, SrO, 1 kind or several kinds of MgO or CaO], Al 2 O 3: 0-10%, GeO 2: 0-10%, Bi 2 O 3: an optical glass containing 0-10%, PbO Provided is the glass which does not contain, has a refractive index range of 1.85 or more, and has an abbe number range of 35-45.
上記光学ガラスは、更にＳｂ２Ｏ３：０−１％、ＳｎＯ２：０−１％、ＣｅＯ２：０−１％を含有しうる。 The optical glass may further Sb 2 O 3: 0-1%, SnO 2: 0-1%, CeO 2: it may contain 0-1%.
上記光学ガラスは、Ｂ２Ｏ３：５−２５％及び／又はＳｉＯ２：０．１−１５％及び／又はＬａ２Ｏ３：３０−５２％及び／又はＧｄ２Ｏ３：５−３５％及び／又はＹ２Ｏ３：１−２０％及び／又はＴａ２Ｏ５：０−５％及び／又はＮｂ２Ｏ５：２−２５％及び／又はＴｉＯ２：０．１−５％及び／又はＺｒＯ２：１−１５％及び／又はＷＯ３：０−５％及び／又はＺｎＯ：０−１０％及び／又はＲ２Ｏ：０−５％及び／又はＲＯ：０−５％及び／又はＡｌ２Ｏ３：０−５％及び／又はＧｅＯ２：０−５％及び／又はＢｉ２Ｏ３：０−５％及び／又はＳｂ２Ｏ３：０−０．５％及び／又はＳｎＯ２：０−０．５％及び／又はＣｅＯ２：０−０．５％を含有しうる。 The optical glass is B 2 O 3 : 5-25% and / or SiO 2 : 0.1-15% and / or La 2 O 3 : 30-52% and / or Gd 2 O 3 : 5-35%. And / or Y 2 O 3 : 1-20% and / or Ta 2 O 5 : 0-5% and / or Nb 2 O 5 : 2-25% and / or TiO 2 : 0.1-5% and / or ZrO 2: 1-15% and / or WO 3: 0-5% and / or ZnO: 0-10% and / or R 2 O: 0-5% and / or RO: 0-5% and / or Al 2 O 3 : 0-5% and / or GeO 2 : 0-5% and / or Bi 2 O 3 : 0-5% and / or Sb 2 O 3 : 0-0.5% and / or SnO 2 : 0-0.5% and / or CeO 2 : 0-0.5% may be contained.
ＳｉＯ２／（ＳｉＯ２＋Ｂ２Ｏ３）の範囲は０．５以下、及び／又はＹ２Ｏ３／（Ｌａ２Ｏ３＋Ｇｄ２Ｏ３＋Ｙ２Ｏ３）は、０．２以下、及び／又はＮｂ２Ｏ５≧ＺｒＯ２。及び／又はＮｂ２Ｏ５／（Ｎｂ２Ｏ５＋ＴｉＯ２＋ＺｒＯ２）の範囲は０．４−０．８、及び／又はＮｂ２Ｏ５＋Ｔａ２Ｏ５＋ＺｒＯ２）／（ＳｉＯ２＋Ｂ２Ｏ３）の範囲は１より小さい；及び／又は（ＺｎＯ＋Ｙ２Ｏ３）／Ｌａ２Ｏ３の範囲は０．０５−０．３でありうる。 The range of SiO 2 / (SiO 2 + B 2 O 3 ) is 0.5 or less, and / or Y 2 O 3 / (La 2 O 3 + Gd 2 O 3 + Y 2 O 3 ) is 0.2 or less, and / Or Nb 2 O 5 ≧ ZrO 2 . And / or the range of Nb 2 O 5 / (Nb 2 O 5 + TiO 2 + ZrO 2 ) is 0.4-0.8, and / or Nb 2 O 5 + Ta 2 O 5 + ZrO 2 ) / (SiO 2 + B 2 O) The range of 3 ) is less than 1; and / or the range of (ZnO + Y 2 O 3 ) / La 2 O 3 can be 0.05-0.3.
ＳｉＯ２／（ＳｉＯ２＋Ｂ２Ｏ３）の範囲は０．２５−０．４、及び／又はＹ２Ｏ３／（Ｌａ２Ｏ３＋Ｇｄ２Ｏ３＋Ｙ２Ｏ３）の範囲は０．０５−０．１２、及び／又はＮｂ２Ｏ５／（Ｎｂ２Ｏ５＋ＴｉＯ２＋ＺｒＯ２）の範囲は０．４８−０．６、及び／又は（Ｎｂ２Ｏ５＋Ｔａ２Ｏ５＋ＺｒＯ２）／（ＳｉＯ２＋Ｂ２Ｏ３）の範囲は０．１−０．９、及び／又は（ＺｎＯ＋Ｙ２Ｏ３）／Ｌａ２Ｏ３の範囲は０．０８−０．１５でありうる。 The range of SiO 2 / (SiO 2 + B 2 O 3 ) is 0.25-0.4, and / or the range of Y 2 O 3 / (La 2 O 3 + Gd 2 O 3 + Y 2 O 3 ) is 0.05. -0.12 and / or Nb 2 O 5 / (Nb 2 O 5 + TiO 2 + ZrO 2 ) ranges from 0.48-0.6 and / or (Nb 2 O 5 + Ta 2 O 5 + ZrO 2 ) / The range of (SiO 2 + B 2 O 3 ) can be 0.1-0.9 and / or the range of (ZnO + Y 2 O 3 ) / La 2 O 3 can be 0.08-0.15.
（Ｎｂ２Ｏ５＋Ｔａ２Ｏ５＋ＺｒＯ２）／（ＳｉＯ２＋Ｂ２Ｏ３）の範囲は０．５−０．８でありうる。 The range of (Nb 2 O 5 + Ta 2 O 5 + ZrO 2 ) / (SiO 2 + B 2 O 3 ) can be 0.5-0.8.
ガラスの屈折率の範囲は１．８７−１．９１でありえ、ガラスのアッベ数の範囲は３７−４１でありうる。 The refractive index range of the glass can be 1.87-1.91 and the Abbe number range of the glass can be 37-41.
ガラスの屈折率の範囲は１．８８−１．９０でありえ、ガラスのアッベ数の範囲は３８−４０でありうる。 The range of refractive index of glass can be 1.88-1.90 and the range of Abbe number of glass can be 38-40.
上記の光学ガラスにより製造されるガラス母材である。 It is a glass base material produced by the above optical glass.
上記の光学ガラスにより製造される光学素子である。 It is an optical element manufactured by the above optical glass.
本発明の有益な効果：ガラス成分のＴａ２Ｏ５含有量を下げ、適量のＬａ２Ｏ３、Ｇｄ２Ｏ３、Ｙ２Ｏ３及びＹｂ２Ｏ３等高屈折率低分散の希土類酸化物を導入し、また、適量比例のＮｂ２Ｏ５或はＴｉＯ２の１種或いは数種を導入して、これら成分の配合比率を最適化し、且つ、ガラスにはＰｂＯが含まず、そのため優れた透過率の高屈折率低分散の環境にやさしい光学ガラスが得られ、また、記述の光学ガラスからなるガラス母材と光学素子が得られる。 Beneficial effect of the present invention: A rare earth oxide having a high refractive index and low dispersion such as La 2 O 3 , Gd 2 O 3 , Y 2 O 3 and Yb 2 O 3 by lowering the Ta 2 O 5 content of the glass component. In addition, one or several kinds of Nb 2 O 5 or TiO 2 in proportion to an appropriate amount were introduced to optimize the blending ratio of these components, and the glass did not contain PbO, so that it was excellent. An environment-friendly optical glass having a high transmittance and a low dispersion can be obtained, and a glass base material and an optical element made of the above-mentioned optical glass can be obtained.
Ｉ．光学ガラス
本明細書において、各組成の含有量、総含有量は特別説明のない限り、重量百分率で示す。更に、ガラス成分の含有量と総含有量の比は重量比で示す。更に、以下の説明において、規定値以下或いは規定値以上の場合も当該規定値を含むものとする。
I. Optical glass In the present specification, the content and total content of each composition are indicated by weight percentage unless otherwise specified. Further, the ratio of the content of the glass component to the total content is indicated by a weight ratio. Furthermore, in the following description, the specified value shall be included even if it is below the specified value or above the specified value.
Ｂ２Ｏ３はガラスの網目形成成分であり、ガラスの可溶性を向上して、ガラス状転移温度を下げる役割をする。上記の効果を達成するため、本発明では１％以上或いはもっと多くのＢ２Ｏ３を取入れるが、その取入れ量が３０％を超えてしまうと、ガラスの安定性が下がり、屈折率も下がり、本発明の高屈折率ガラスは得られなくなる。従って、１−３０％のＢ２Ｏ３を取入れ、好ましくはＢ２Ｏ３を５−２５％取り入れ、更に好ましくは７−２０％を取入れる。 B 2 O 3 is a network-forming component of glass and plays a role of improving the solubility of glass and lowering the vitreous transition temperature. In order to achieve the above effects, 1% or more or more B 2 O 3 is incorporated in the present invention, but if the incorporated amount exceeds 30%, the stability of the glass decreases and the refractive index also decreases. , The high refractive index glass of the present invention cannot be obtained. Therefore, 1-30% of B 2 O 3 is incorporated, preferably 5-25% of B 2 O 3 is incorporated, and more preferably 7-20% is incorporated.
ＳｉＯ２はガラスの熱安定性の役割を有し、ガラス溶融及び形成時の粘度を上げることができる。但し、その含有量が２０％を超えてしまうと、ガラスは溶けにくくなり、本発明の屈折率が得られなくなる。従って、本発明のＳｉＯ２の含有量は０−２０％とし、好ましくはＳｉＯ２含有量を０．１−１５％とし、更に好ましくは３−１２％とする。 SiO 2 has a role of thermal stability of the glass and can increase the viscosity at the time of glass melting and formation. However, if the content exceeds 20%, the glass becomes difficult to melt and the refractive index of the present invention cannot be obtained. Therefore, the content of SiO 2 of the present invention is 0 to 20%, preferably the content of SiO 2 is 0.1 to 15%, and more preferably 3 to 12%.
ガラスの溶融性を改善し、ガラスの安定性及び溶融ガラス成形に適切な粘性を維持するため、本発明で導入するＳｉＯ２含有量はより小なりイコールＢ２Ｏ３の含有量で、即ちＳｉＯ２≦Ｂ２Ｏ３である。 In order to improve the meltability of the glass and maintain the stability of the glass and the viscosity suitable for molten glass molding, the SiO 2 content introduced in the present invention is smaller and equal to the content of B 2 O 3 , that is, SiO. 2 ≤ B 2 O 3 .
また透過率の高いガラスを得るために、ガラス的溶融温度の上昇を抑制し、溶融ガラスに溶融する白金イオン等着色を悪化させる物質の混入量を減少・抑制し、本発明ガラスのアッベ数範囲を効果的に調整する為、本発明ではＳｉＯ２／（ＳｉＯ２＋Ｂ２Ｏ３）範囲を好ましくは０．５以下とし、更に好ましくは０．１−０．４５とし、より更に好ましくは０．２５−０．４範囲とする。 Further, in order to obtain a glass having high transmittance, an increase in the glass-like melting temperature is suppressed, and the amount of a substance that worsens coloring such as platinum ions melted in the molten glass is reduced / suppressed, and the Abbe number range of the glass of the present invention is obtained. In the present invention, the SiO 2 / (SiO 2 + B 2 O 3 ) range is preferably 0.5 or less, more preferably 0.1-0.45, and even more preferably 0. The range is 25-0.4.
Ｌａ２Ｏ３は、本発明の必要な光学特性を得る必須組成である。Ｌａ２Ｏ３の含有量が２５％より小さい場合は、必要な光学特性は果たせなくなる。但しその含有量が５５％を超えてしまうと、ガラスの耐失透性と溶融性能が全て悪化してしまう。そのため、本発明のＬａ２Ｏ３の含有量は２５−５５％とし、好ましくは３０−５２％とし、更に好ましくは３５−５０％とする。 La 2 O 3 is an essential composition for obtaining the required optical properties of the present invention. If the content of La 2 O 3 is less than 25%, the required optical properties cannot be achieved. However, if the content exceeds 55%, the devitrification resistance and melting performance of the glass are all deteriorated. Therefore, the content of La 2 O 3 of the present invention is 25-55%, preferably 30-52%, and more preferably 35-50%.
本発明ではＧｄ２Ｏ３とＬａ２Ｏ３が共存することによって、形成するガラスの安定性を向上することができる。但し、Ｇｄ２Ｏ３の含有量が５％以下の場合は、上記の効果は明らかでない。その含有量が４０％を超えてしまうと、ガラスの耐失透性が低下し、ガラスの安定性が悪くなってしまう。従って、本発明ではＧｄ２Ｏ３の含有量は５−４０％で、好ましくは５−３５％範囲とし、更に好ましくは１０−３０％範囲とする。 In the present invention, the coexistence of Gd 2 O 3 and La 2 O 3 can improve the stability of the formed glass. However, when the content of Gd 2 O 3 is 5% or less, the above effect is not clear. If the content exceeds 40%, the devitrification resistance of the glass is lowered and the stability of the glass is deteriorated. Therefore, in the present invention, the content of Gd 2 O 3 is 5-40%, preferably in the range of 5-35%, and more preferably in the range of 10-30%.
本発明の高屈折低分散作用の組成では、好ましくはＹ２Ｏ３を取入れる事によって、ガラスの溶融性、耐失透性を改善することが出来、更にガラスの結晶上限温度を下げることができるが、その含有量が２５％を超えてしまうと、ガラスの安定性、耐失透性が下がってしまう。そのため、Ｙ２Ｏ３の含有量範囲は０−２５％とし、好ましくは０−２０％範囲とし、更に好ましくは２−１５％範囲とする。 The composition of the high refractive index and low dispersion effect of the present invention, preferably by introducing a Y 2 O 3, glass meltability, it is possible to improve devitrification resistance, can further reduce the crystal upper limit temperature of the glass However, if the content exceeds 25%, the stability and devitrification resistance of the glass will decrease. Therefore, the content range of Y 2 O 3 is 0 to 25%, preferably 0 to 20%, and more preferably 2 to 15%.
Ｙｂ２Ｏ３も高屈折、低分散性能の組成を付与された物で、その取入れ量が１０％超えてしまうと、ガラスの耐結晶性能が下がるので、その含有量を好ましくは０−１０％とする。更にＹｂ２Ｏ３はＧｄ２Ｏ３、Ｙ２Ｏ３に比べて比較的に高価であり、ガラスの溶融性能の改善に作用は少ないので、好ましくは導入しない。 Yb 2 O 3 is also given a composition of high refraction and low dispersion performance, and if the amount of Yb 2 O 3 taken in exceeds 10%, the crystal resistance of the glass decreases, so the content is preferably 0-10%. And. Further, Yb 2 O 3 is relatively expensive as compared with Gd 2 O 3 and Y 2 O 3 , and has little effect on improving the melting performance of glass, and therefore is not preferably introduced.
Ｌａ２Ｏ３、Ｇｄ２Ｏ３、Ｙ２Ｏ３とＹｂ２Ｏ３において、ガラスの屈折率を向上して、且つガラスの安定性を維持する一番大きな成分はＬａ２Ｏ３である。但し、本発明の光学ガラスはＬａ２Ｏ３のみ使う場合は、充分なガラスの安定性を保証することが難しい。従って、本発明ではＬａ２Ｏ３成分の導入量が一番多く、更にＬａ２Ｏ３とＧｄ２Ｏ３を共存させる。或いは好ましくはＬａ２Ｏ３、Ｇｄ２Ｏ３とＹ２Ｏ３を共存させる。更に好ましくはＹ２Ｏ３／（Ｌａ２Ｏ３＋Ｇｄ２Ｏ３＋Ｙ２Ｏ３＋Ｙｂ２Ｏ３）を０．２以下とし、より更に好ましくはＹ２Ｏ３／（Ｌａ２Ｏ３＋Ｇｄ２Ｏ３＋Ｙ２Ｏ３）を０．０１−０．１５とし、更に一歩好ましくはＹ２Ｏ３／（Ｌａ２Ｏ３＋Ｇｄ２Ｏ３＋Ｙ２Ｏ３）を０．０５−０．１２とすることで、優れるガラス安定性を有する高屈折率低分散のガラスが得られ、同時にガラスは着色し難い。 In La 2 O 3 , Gd 2 O 3 , Y 2 O 3 and Y b 2 O 3 , the largest component that improves the refractive index of glass and maintains the stability of glass is La 2 O 3 . However, when the optical glass of the present invention uses only La 2 O 3, it is difficult to guarantee sufficient glass stability. Therefore, in the present invention, the amount of the La 2 O 3 component introduced is the largest, and La 2 O 3 and Gd 2 O 3 coexist. Alternatively, La 2 O 3 , Gd 2 O 3 and Y 2 O 3 coexist. More preferably, Y 2 O 3 / (La 2 O 3 + Gd 2 O 3 + Y 2 O 3 + Yb 2 O 3 ) is 0.2 or less, and even more preferably Y 2 O 3 / (La 2 O 3 + Gd 2 O). 3 + Y 2 O 3 ) should be 0.01-0.15, and one step more preferably Y 2 O 3 / (La 2 O 3 + Gd 2 O 3 + Y 2 O 3 ) should be 0.05-0.12. As a result, a glass having a high refractive index and a low dispersion having excellent glass stability can be obtained, and at the same time, the glass is difficult to color.
Ｎｂ２Ｏ５はガラスの屈折率と分散を向上する役割を有し、ガラスの耐結晶性と化学耐久性を向上する役割を有する。但しＮｂ２Ｏ５の含有量が１％未満の場合は、上記の効果は得られなくなる。その含有量が３０％を超えてしまうと、ガラスの分散が向上され、本発明のガラスの光学特性は果たせなく、耐失透性も悪化してしまう。そのため、Ｎｂ２Ｏ５の含有量範囲は１−３０％とし、好ましくは２−２５％範囲とし、更に好ましくは３−２０％範囲とし、より更に好ましくは４−１５％範囲とする。 Nb 2 O 5 has a role of improving the refractive index and dispersion of glass, and has a role of improving crystallinity and chemical durability of glass. However, if the content of Nb 2 O 5 is less than 1%, the above effect cannot be obtained. If the content exceeds 30%, the dispersion of the glass is improved, the optical characteristics of the glass of the present invention cannot be achieved, and the devitrification resistance is also deteriorated. Therefore, the content range of Nb 2 O 5 is 1-30%, preferably 2-25%, more preferably 3-20%, and even more preferably 4-15%.
Ｔａ２Ｏ５はガラスの屈折率を向上する役割を有し、同時にガラスの低分散を維持する役割がＮｂ２Ｏ５より優れる。ガラスの安定性を更に改善する必要がある場合は、少量のＴａ２Ｏ５を導入することで一部のＮｂ２Ｏ５を代替することができる。但し、その他の成分と比べＴａ２Ｏ５は非常に高価であるため、本発明の実用性及び原価から勘案してその使用量を減少した。本発明のＴａ２Ｏ５含有量は０−１０％で、好ましくは０−５％範囲で、更に好ましくは導入しない。 Ta 2 O 5 has a role of improving the refractive index of glass, and at the same time, has a role of maintaining low dispersion of glass, which is superior to Nb 2 O 5 . If the stability of the glass needs to be further improved, some Nb 2 O 5 can be replaced by introducing a small amount of Ta 2 O 5 . However, since Ta 2 O 5 is very expensive as compared with other components, the amount used has been reduced in consideration of the practicality and cost of the present invention. The Ta 2 O 5 content of the present invention is 0-10%, preferably in the range of 0-5%, and more preferably not introduced.
ＴｉＯ２もガラス屈折率を向上する役割を有し、更にガラス網目形成に参加し、適量な導入はガラスが更に安定させる。但し、その含有量があまりにも多くなると、ガラス分散が明らかに増やし、同時にガラスの可視光エリアの短波部分の透射率が低下され、ガラスの着色傾向が増加される。そのため、本発明では好ましくはＴｉＯ２の含有量を０−１０％とし、更に好ましくはＴｉＯ２の含有量を０．１−５％とし、より更に好ましくは０．５−３％範囲とする。 TiO 2 also has a role of improving the refractive index of glass, further participates in the formation of a glass network, and the introduction of an appropriate amount further stabilizes the glass. However, if the content is too high, the glass dispersion is clearly increased, and at the same time, the transmittance of the short wave portion of the visible light area of the glass is lowered, and the coloring tendency of the glass is increased. Therefore, preferably in the present invention the content of TiO 2 and 0-10%, more preferably the content of TiO 2 and 0.1-5%, even more preferably at 0.5-3% range.
本発明ガラス成分にＴａ２Ｏ５の導入量が低下或いは導入しない場合は、Ｎｂ２Ｏ５或いはＴｉＯ２を導入することによって、好ましくはＴｉＯ２とＮｂ２Ｏ５をガラス成分として共存させ、更に好ましくはＴｉＯ２／Ｎｂ２Ｏ５を０．３以下に抑制し、より更に好ましくはＴｉＯ２／Ｎｂ２Ｏ５を０．２５以下とし、より一歩更に好ましくはＴｉＯ２／Ｎｂ２Ｏ５を０．２以下とすることで、高屈折低分散を実現し、ガラス着色度を抑制すると同時に、ガラスの安定性が優れる。 When the amount of Ta 2 O 5 introduced into the glass component of the present invention is reduced or not introduced, Nb 2 O 5 or TiO 2 is introduced, preferably TiO 2 and Nb 2 O 5 coexist as the glass component, and further. Preferably, TiO 2 / Nb 2 O 5 is suppressed to 0.3 or less, further preferably TiO 2 / Nb 2 O 5 is set to 0.25 or less, and even more preferably dio 2 / Nb 2 O 5 is set to 0. By setting it to .2 or less, high refraction and low dispersion are realized, the degree of glass coloring is suppressed, and at the same time, the stability of the glass is excellent.
本発明は少量のＺｒＯ２を導入することによって、ガラス屈折率と安定性を向上し、０．５％或いはもっと多くのＺｒＯ２を導入することができる。但し、ＺｒＯ２導入量が２０％を超えてしまうと、ガラスは溶け難く、均一なガラスが得られなくなる。そのため、本発明のＺｒＯ２の含有量範囲は０．５−２０％とし、好ましい含有量範囲は１−１５％とし、更に好ましい範囲は３−１０％とする。 The present invention can improve the glass refractive index and stability by introducing a small amount of ZrO 2, and can introduce 0.5% or more ZrO 2 . However, if the amount of ZrO 2 introduced exceeds 20%, the glass is difficult to melt and a uniform glass cannot be obtained. Therefore, the content range of ZrO 2 of the present invention is 0.5-20%, the preferable content range is 1-15%, and the more preferable range is 3-10%.
本発明では好ましくはガラス成分にＮｂ２Ｏ５の導入量を大なりイコールＺｒＯ２とし、即ちＮｂ２Ｏ５≧ＺｒＯ２とし、ガラスの着色を効果的に抑制し、且つガラスの耐失透性能を向上する。本発明では、更に好ましくはＮｂ２Ｏ５／（Ｎｂ２Ｏ５＋ＴｉＯ２＋ＺｒＯ２）を０．４−０．８範囲とし、更に好ましくは０．４５−０．７の範囲とし、より更に好ましくは０．４８−０．６の範囲とし、ガラスの着色をより良く抑制し、ガラスの透過率を向上する事ができる。 In the present invention, preferably, the amount of Nb 2 O 5 introduced into the glass component is set to be equal to ZrO 2 , that is, Nb 2 O 5 ≥ ZrO 2 , the coloring of the glass is effectively suppressed, and the devitrification resistance of the glass is achieved. To improve. In the present invention, Nb 2 O 5 / (Nb 2 O 5 + TiO 2 + ZrO 2 ) is more preferably in the range of 0.4-0.8, still more preferably in the range of 0.45-0.7, and even more preferably. Is in the range of 0.48-0.6, and the coloring of the glass can be better suppressed and the transmittance of the glass can be improved.
本発明では好ましくはＮｂ２Ｏ５、Ｔａ２Ｏ５とＺｒＯ２の合計量を抑制している。（Ｎｂ２Ｏ５＋Ｔａ２Ｏ５＋ＺｒＯ２）とＳｉＯ２とＢ２Ｏ３の合計量（ＳｉＯ２＋Ｂ２Ｏ３）の比で、好ましくは（Ｎｂ２Ｏ５＋Ｔａ２Ｏ５＋ＺｒＯ２）／（ＳｉＯ２＋Ｂ２Ｏ３）の比を１より小さくし、更に好ましくは０．１−０．９範囲とし、より更に好ましくは０．５−０．８範囲として、本発明で好ましく選定した屈折率とアッベ数範囲を実現すると同時に、ガラスの着色を効果的に抑制し、ガラスの熱安定性と耐失透性能を向上する。 In the present invention, the total amount of Nb 2 O 5 , Ta 2 O 5 and ZrO 2 is preferably suppressed. The total amount of (Nb 2 O 5 + Ta 2 O 5 + ZrO 2) and SiO 2, B 2 O 3 at a ratio of (SiO 2 + B 2 O 3 ), preferably (Nb 2 O 5 + Ta 2 O 5 + ZrO 2) / The refractive index preferably selected in the present invention is such that the ratio of (SiO 2 + B 2 O 3 ) is smaller than 1, more preferably 0.1-0.9 range, and even more preferably 0.5-0.8 range. At the same time as achieving the rate and Abbe number range, it effectively suppresses the coloring of the glass and improves the thermal stability and devitrification resistance of the glass.
ＷＯ３は屈折率を向上する役割をするが、その含有量が１０％を超えてしまうと、分散が著しく高くなり、かつ、ガラスの可視光エリアの短波の長い側の投射率を低下させ、着色の増加傾向があるため、本発明ではＷＯ３の含有量を好ましくは０−１０％とし、更に好ましくは０−５％とし、より更に好ましくは０−３％とし、より一歩好ましくは導入しないことである。 WO 3 plays a role in improving the refractive index, but when the content exceeds 10%, the dispersion becomes remarkably high and the projection rate on the long side of the short wave in the visible light area of the glass is lowered. In the present invention, the content of WO 3 is preferably 0-10%, more preferably 0-5%, even more preferably 0-3%, and even more preferably not introduced because of the increasing tendency of coloring. That is.
適量のＺｎＯはガラスの安定性或いは溶融性を改善し、加圧成形を改善する役割をするが、その含有量が余りにも高くなると、屈折率が下がって、本発明の要求を満たさず、ガラスの耐失透性も下がり、液相温度が上昇してしまう。そのため、本発明ではＺｎＯの含有量を０−１５％とし，好ましくはＺｎＯの含有量は０−１０とし、更に好ましくはＺｎＯの含有量を０−５％とし、より更に好ましくは導入しない。 An appropriate amount of ZnO plays a role of improving the stability or meltability of the glass and improving the pressure molding, but if the content is too high, the refractive index is lowered and the requirement of the present invention is not satisfied, and the glass is not satisfied. The devitrification resistance of the glass also decreases, and the liquidus temperature rises. Therefore, in the present invention, the ZnO content is 0-15%, preferably the ZnO content is 0-10, more preferably the ZnO content is 0-5%, and even more preferably no introduction.
本発明のガラス成分の好ましくは（ＺｎＯ＋Ｙ２Ｏ３）／Ｌａ２Ｏ３の範囲を０．５以下とし、更に好ましくは０．０５−０．３範囲とし、より更に好ましくは０．０８−０．１５範囲とし、ガラス安定性と転移温度の低下改善に更に有利である。 The glass component of the present invention preferably has a range of (ZnO + Y 2 O 3 ) / La 2 O 3 of 0.5 or less, more preferably 0.05-0.3, and even more preferably 0.08-0. The range is .15, which is more advantageous for improving glass stability and lowering of transition temperature.
Ｒ２Ｏ（Ｒ２ＯはＬｉ２Ｏ、Ｎａ２Ｏ或いはＫ２Ｏの１種或いは数種）はガラスの熔融性を改善して、ガラス化転移温度を下げることができるが、その含有量が１０％を超える場合は、ガラス安定性が悪くなり、屈折率が大幅に低下してしまうので、本発明ではＲ２Ｏの含有量を好ましくは０−１０とし、更に好ましくは含有量範囲を０−５％とし、より更に好ましくは導入しない。 R 2 O (R 2 O is one or several of Li 2 O, Na 2 O or K 2 O) can improve the meltability of glass and lower the vitrification transition temperature, but its content. If There more than 10%, the glass stability is degraded, the refractive index is greatly reduced, preferably the content of R 2 O in the present invention is a 0-10, more preferably the content ranges It is set to 0-5%, and more preferably it is not introduced.
ＲＯ（ＲＯはＢａＯ、ＳｒＯ、ＣａＯ或いはＭｇＯの１種或いは数種）はガラスの熔融性を改善して、ガラス化転移温度を低減することができるが、その含有量が１０％を超える場合は、ガラスの耐失透性下がるため、本発明ではＲＯの含有量を好ましくは０−１０％とし、更に好ましくは０−５％範囲で、より更に好ましくは導入しない。 RO (RO is one or several of BaO, SrO, CaO or MgO) can improve the meltability of glass and reduce the vitrification transition temperature, but if its content exceeds 10% In the present invention, the RO content is preferably 0-10%, more preferably 0-5%, and even more preferably not introduced, because the devitrification resistance of the glass is lowered.
少量のＡｌ２Ｏ３の導入はガラスの安定性と化学安定性を改善できるが、その含有量が１０％を超える場合は、ガラスの溶融性が悪くなり、耐失透性が低下する傾向があり、そのため、本発明では、Ａｌ２Ｏ３の含有量を好ましくは０−１０％とし、更に好ましくは０−５％とし、より更に好ましくは導入しないことである。 The introduction of a small amount of Al 2 O 3 can improve the stability and chemical stability of the glass, but if the content exceeds 10%, the meltability of the glass deteriorates and the devitrification resistance tends to decrease. Therefore, in the present invention, the content of Al 2 O 3 is preferably 0-10%, more preferably 0-5%, and even more preferably not introduced.
Ｂｉ２Ｏ３はガラス屈折率を向上する事ができるが、過量に含有する場合は、可視光エリアの短波の長い側の投射率が低下してしまう場合があって、ガラスに着色の傾向が発生してしまうので、本発明ではＢｉ２Ｏ３含有量を好ましくは０−１０％とし、更に好ましくは０−５％とし、より更に好ましくは導入しないことである。 Bi 2 O 3 can improve the refractive index of glass, but if it is contained in an excessive amount, the projection rate on the long side of the short wave in the visible light area may decrease, and the glass tends to be colored. In the present invention, the Bi 2 O 3 content is preferably 0-10%, more preferably 0-5%, and even more preferably not introduced.
ＧｅＯ２もガラスの安定性と耐失透性を改善する役割をするが、ＧｅＯ２は高価な成分であるため、ＧｅＯ２の含有量を好ましくは０−１０％とし、更に好ましくは０−５％とし、より更に好ましくは導入しないことである。 GeO 2 also plays a role in improving the stability and devitrification resistance of glass, but since Geo 2 is an expensive component, the content of Geo 2 is preferably 0-10%, more preferably 0-5. %, More preferably not introduced.
少量なＳｂ２Ｏ３、ＳｎＯ２、ＣｅＯ２成分を添加することにより、ガラスの澄清効果があるが、Ｓｂ２Ｏ３の含有量が１％を超えてしまうと、ガラスの澄清性能が低下する傾向があり、強い酸化作用によって成形型の悪化を促すので、本発明ではＳｂ２Ｏ３の添加量を好ましくは０−１％とし、更に好ましくは０−０．５％とし、より更に好ましくは導入しないことである。ＳｎＯ２も澄清剤として添加できるが、その含有量が１％を超えてしまうと、ガラスは着色することが出来、或いはガラスを加熱、難化してモールド成形等二次成形を行う際、Ｓｎは結晶核生成のスタートポイントとなり、失透の傾向が生じてしまう。そのため、本発明のＳｎＯ２の含有量は好ましくは０−１％とし、更に好ましくは０−０．５％とし、より更に好ましくは導入しないことである。ＣｅＯ２の役割及び添加量比例はＳｎＯ２と一致し、その含有量は好ましくは、０−１％とし、更に好ましくは０−０．５％とし、より更に好ましくは導入しないことである。 The addition of a small amount of Sb 2 O 3 , SnO 2 , and CeO 2 components has a clearing effect on the glass, but if the content of Sb 2 O 3 exceeds 1%, the clearing performance of the glass deteriorates. Since there is a tendency and the strong oxidizing action promotes deterioration of the molding mold, the amount of Sb 2 O 3 added in the present invention is preferably 0-1%, more preferably 0-0.5%, and even more preferably. Do not introduce it. SnO 2 can also be added as a clearing agent, but if the content exceeds 1%, the glass can be colored, or when the glass is heated and made difficult to perform secondary molding such as molding, Sn can be added. It becomes the starting point for crystal nucleation and tends to be devitrified. Therefore, the content of SnO 2 of the present invention is preferably 0-1%, more preferably 0-0.5%, and even more preferably not introduced. The role of CeO 2 and the proportion of the amount added are consistent with SnO 2, and the content thereof is preferably 0-1%, more preferably 0-0.5%, and even more preferably no introduction.
この他、ガラス原料は、硝酸塩、炭酸塩或いは硫酸塩の形で導入し、脱泡性も向上することができる。本発明において、Ｓｂ２Ｏ３、ＳｎＯ２或いはＣｅＯ２の１種或いは数種と前述の硝酸塩、炭酸塩或いは硫酸塩の１種或いは数種の組み合わせによって使用することも出来、全て効果がある。 In addition, the glass raw material can be introduced in the form of nitrate, carbonate or sulfate, and the defoaming property can be improved. In the present invention, it can also be used by one or several combinations of Sb 2 O 3 , SnO 2 or CeO 2 and one or several of the above-mentioned nitrates, carbonates or sulfates, all of which are effective.
Ｆは低分散化、ガラス化転移温度を低下する有効な成分であるが、過量に含有する場合は、ガラス屈折率が著しく低下、或いはガラス溶液の揮発性が増大し、ガラス溶液が成形の際に縞が発生し、或いは揮発により屈折率の変動が増大する傾向が生じる。Ｆは、原料としてＹＦ３、ＬａＦ３、ＹｂＦ３、ＺｒＦ４、ＺｎＦ２、アルカリ金属フッ化物或いはアルカリ性金属フッ化物を導入することができる。Ｆの導入量は、ガラス陰イオン総量が１００％の場合の、ガラス中の Ｆイオン百分比で考えられる。陰イオン百分比で計上する場合、本発明ではＦの含有量は好ましくは０−３０％とし、更に好ましくは０−２０％とし、より更に好ましくは導入しないことである。 F is an effective component that lowers the dispersion and the vitrification transition temperature, but if it is contained in an excessive amount, the refractive index of the glass is significantly reduced or the volatility of the glass solution is increased, and the glass solution is formed during molding. There is a tendency for the fluctuation of the refractive index to increase due to the occurrence of stripes or volatilization. For F, YF 3 , LaF 3 , YbF 3 , ZrF 4 , ZnF 2 , alkali metal fluoride or alkaline metal fluoride can be introduced as a raw material. The amount of F introduced can be considered as the percentage of F ions in the glass when the total amount of glass anions is 100%. When counted as an anion percentage, the content of F in the present invention is preferably 0-30%, more preferably 0-20%, and even more preferably not introduced.
［光学ガラスの光学特性］
以下、本発明の光学ガラスの特性について詳細に説明する。
[Optical characteristics of optical glass]
Hereinafter, the characteristics of the optical glass of the present invention will be described in detail.
本発明の光学ガラスは高屈折率・低分散ガラスであり、高屈折率・低分散ガラスより製造されたレンズの多くは高屈折率高分散ガラスより製造されたレンズと組合せて、色差校正に用いる。本発明の光学ガラスは、その用途の光学特性に適用する角度から勘案して、ガラス屈折率範囲を１．８５以上とし、好ましくは１．８７−１．９１範囲とし、更に好ましくは１．８８−１．８９範囲とする。本発明ガラスのアッベ数νｄの範囲は３５−４５で、好ましくは３７−４１範囲とし、更に好ましくは３８−４０範囲とする。 The optical glass of the present invention is a high-refractive-index, low-dispersion glass, and most of the lenses manufactured from the high-refractive-index, low-dispersion glass are used for color difference calibration in combination with a lens manufactured from the high-refractive-index, high-dispersion glass. .. The optical glass of the present invention has a glass refractive index range of 1.85 or more, preferably 1.87-1.91 range, and more preferably 1.88, in consideration of the angle applied to the optical characteristics of the application. -The range is 1.89. The Abbe number ν d of the glass of the present invention is in the range of 35-45, preferably in the range of 37-41, and more preferably in the range of 38-40.
［光学ガラスの着色］
本発明ガラスの短波透射スペクトル特性は着色度（λ７０／λ５）で表す。λ７０とは、ガラス透過率が７０％達する時に対応する波長の事を指し、λ５とは、ガラス透過率が５％達する時に対応する波長の事を指す。その内、λ７０の測定は相互並行して且つ、光学研磨の二つの相対平面で厚さが１０±０．１ｍｍのガラスを使って、２８０ｎｍから７００ｎｍまでの波長域内の分光透過率を測定して、且つ透過率７０％の波長を表す。所謂分光透過率或いは透過率とは、ガラスの上記表面に強度Ｉｉｎの光を垂直に入射して、ガラスを透過して、異なる平面から強度Ｉｏｕｔの光を入射する状況において、Ｉｏｕｔ／Ｉｉｎによって表示する量であり、また、ガラスの上記表面上の表面反射損失の透過率を含んだ。ガラスの屈折率が高いほど、表面反射損失は大きい。そのため、高屈折率ガラスにおいては、λ７０の値が小さければ、ガラス自体の着色は極めて少ない。
[Coloring of optical glass]
The short-wave transmission spectral characteristics of the glass of the present invention are represented by the degree of coloring (λ 70 / λ 5 ). λ 70 refers to the wavelength corresponding to the glass transmittance reaching 70%, and λ 5 refers to the wavelength corresponding to the glass transmittance reaching 5%. Among them, the measurement of λ 70 is performed in parallel, and the spectral transmittance in the wavelength range from 280 nm to 700 nm is measured using glass having a thickness of 10 ± 0.1 mm on two relative planes of optical polishing. And represents a wavelength with a transmittance of 70%. The so-called spectral transmittance or transmittance, the light intensity I in the above surface of the glass is perpendicularly incident transmitted through the glass, in the context of the incident light of intensity I out from different planes, I out / It is the amount indicated by I in and also includes the transmittance of the surface reflection loss on the surface of the glass. The higher the refractive index of glass, the greater the surface return loss. Therefore, in high-refractive index glass, if the value of λ 70 is small, the coloring of the glass itself is extremely small.
本発明の光学ガラスのλ７０は、４１０ｎｍより小か等しい、好ましくはλ７０の範囲は４００ｎｍより小か等しい、更に好ましくはλ７０の範囲は３８５ｎｍより小か等しい、より更に好ましくはλ７０の範囲は３７８−３８５ｎｍで、より一層更に好ましくはλ７０の範囲は３７８−３８０ｎｍである。 The λ 70 of the optical glass of the present invention is less than or equal to 410 nm, preferably the range of λ 70 is less than or equal to 400 nm, more preferably the range of λ 70 is less than or equal to 385 nm, even more preferably of λ 70 . The range is 378-385 nm, and even more preferably the range of λ 70 is 378-380 nm.
λ７０を４１０ｎｍより小か等しくさせることにより、色彩バランスが優れる撮影光学系統或いは投射光学系統の光学素子が得られる。この他、着色が少なく、かつ、高屈折率低分散性が有るため、撮影光学系統と投射光学系統のコンパクト化させることができる。これにより、本発明の光学ガラスは、撮影光学系統と投射光学系統を構成する光学素子の材料に適切し、特に、一眼レフカメラの交換レンズの光学素子用材料に適合する。 By making λ 70 smaller or equal to less than 410 nm, an optical element of a photographing optical system or a projection optical system having an excellent color balance can be obtained. In addition, since there is little coloring and high refractive index and low dispersibility, the photographing optical system and the projection optical system can be made compact. As a result, the optical glass of the present invention is suitable as a material for the optical element constituting the photographing optical system and the projection optical system, and is particularly suitable for the material for the optical element of the interchangeable lens of the single-lens reflex camera.
［光学ガラスの転移温度］
光学ガラスは、ある温度区間で徐々に固体状態から可塑態変わる。転移温度とは、ガラス試料が室温から撓み温度まで昇温し、その低温エリアと高温エリアの直線部分の延長線が交差する接点の対応する温度を言う。
[Transition temperature of optical glass]
Optical glass gradually changes from a solid state to a plastic state in a certain temperature interval. The transition temperature refers to the corresponding temperature of the contact point where the glass sample rises from room temperature to the bending temperature and the extension line of the straight portion of the low temperature area and the high temperature area intersect.
本発明ガラスの転移温度Ｔｇは７３５℃以下で、好ましくは、７１０−７３５℃とし、更に好ましくは７１５−７２５℃とする。 The transition temperature Tg of the glass of the present invention is 735 ° C. or lower, preferably 710-735 ° C., and more preferably 715-725 ° C.
［光学ガラスの化学安定性］
光学ガラス素子は製造及び使用において、その研磨表面が各種の侵蝕介在作用を抵抗する能力を光学ガラスの化学安定性と称する。
[Chemical stability of optical glass]
In the manufacture and use of optical glass elements, the ability of the polished surface to resist various erosion-mediated actions is referred to as the chemical stability of optical glass.
本発明ガラスの耐水作用安定性ＤＷ（粉末法）、耐酸作用安定性ＤＡ（粉末法）は全て２類以上で、好ましくは１類以上である。 Water acts stability D W of the present invention the glass (powder method), acid acting stability D A (powder method) on all Class 2 or more, preferably more than 1 class.
上記耐水作用安定性ＤＷ（粉末法）は、ＧＢ／Ｔ１７１２９の測定方法により、下記の式に基づいて算出する： The water resistance stability D W (powder method) is calculated based on the following formula by the measurement method of GB / T17129:
ＤＷ＝（Ｂ−Ｃ）／（Ｂ−Ａ）＊１００
式において：ＤＷ−ガラス浸出百分率（％）
Ｂ−ろ過器と試料の質量（ｇ）
Ｃ−ろ過器と侵蝕後試料の質量（ｇ）
Ａ−ろ過器質量（ｇ）
により計算して得られる浸出百分率は、光学ガラス耐水作用安定ＤＷを６類に分類し、詳細は下表による。
D W = (BC) / (BA) * 100
In the formula: DW -Glass leaching percentage (%)
B-Filter and sample mass (g)
Mass of C-filter and post-erosion sample (g)
A-filter mass (g)
The leaching percentage obtained by the above is classified into 6 types of optical glass water resistant action stable DW , and the details are shown in the table below.
上記耐酸作用安定性ＤＡ（粉末法）は、ＧＢ／Ｔ１７１２９の測定方法により、下記の式に基づいて算出する： The acid acts stability D A (powder method), by a measuring method of GB / T17129, calculated based on the following equation:
ＤＡ＝（Ｂ−Ｃ）／（Ｂ−Ａ）＊１００
式において：ＤＡ−ガラス浸出百分率（％）
Ｂ−ろ過器と試料の質量（ｇ）
Ｃ−ろ過器と侵蝕後試料の質量（ｇ）
Ａ−ろ過器質量（ｇ）
計算によって得られる浸出百分率は、光学ガラス耐酸作用安定ＤＡを６類に分類し、詳細は下表による。
D A = (B-C) / (B-A) * 100
In the formula: D A - Glass leaching percentage (%)
B-Filter and sample mass (g)
Mass of C-filter and post-erosion sample (g)
A-filter mass (g)
Leaching percentage obtained by calculation, the optical glass acid acts stably D A classified into 6 acids, are by the following table details.
［光学ガラスの密度］
光学ガラスの密度は、温度が２０℃時の単位体積の質量で、単位はｇ／ｃｍ３で表示する。
本発明ガラスの密度は、５．３ｇ／ｃｍ３以下で、好ましくは５．１５−５．３ｇ／ｃｍ３とし、更に好ましくは５．１５−５．２ｇ／ｃｍ３とする。
[Density of optical glass]
The density of optical glass is the mass of a unit volume when the temperature is 20 ° C., and the unit is expressed in g / cm 3 .
Density of the present invention the glass is a 5.3 g / cm 3 or less, preferably a 5.15-5.3g / cm 3, further preferably 5.15-5.2g / cm 3.
II．光学母材及び光学素子
以下、本発明の光学母材及び光学素子を説明する。
II. Optical base material and optical element The optical base material and optical element of the present invention will be described below.
本発明の光学母材及び光学素子は、全て上記本発明の光学ガラスからなる。本発明の光学母材は、高屈折率・低分散特性を有する。本発明の光学素子は、高屈折率・低分散特性を有し、低コストで光学価値の高い各種レンズ、プリズム等光学素子を提供することができる。 The optical base material and the optical element of the present invention are all made of the above-mentioned optical glass of the present invention. The optical base material of the present invention has high refractive index and low dispersion characteristics. The optical element of the present invention has high refractive index and low dispersion characteristics, and can provide various optical elements such as lenses and prisms having high optical value at low cost.
レンズの例として、レンズ面が球面或いは非球面の凹面のメニスカスレンズ、凸面のメニスカスレンズ、両凸レンズ、両凹レンズ、平凸レンズ、平凹レンズ等各種レンズがある。
これらレンズは、高屈折率高分散ガラスより製造されたレンズと組合せて、色差校正をすることができ、色差校正用のレンズに適切する。また、光学体系のコンパクト化にも非常に有效なレンズである。
Examples of the lens include various lenses such as a concave meniscus lens having a spherical or aspherical lens surface, a convex meniscus lens, a biconvex lens, a biconcave lens, a plano-convex lens, and a plano-concave lens.
These lenses can be chromatically calibrated in combination with a lens manufactured of high refractive index and highly dispersed glass, and are suitable as lenses for chromatic aberration calibration. It is also a very effective lens for making the optical system compact.
プリズムにとっては、屈折率が高い為、撮影光学体系に組合せすることによって、屈曲光路を経由して、必要とする方向へ向けば、即ち、コンパクトで、広角の光学体系を実現できる。 Since the refractive index of a prism is high, by combining it with a photographing optical system, it is possible to realize a compact and wide-angle optical system by directing it in a required direction via a bending optical path.
本発明の課題を解決するための手段として、以下、実施例を挙げて本発明の光学ガラスを更に詳細に説明するが、本発明はこれらの実施例に限られない。 Hereinafter, the optical glass of the present invention will be described in more detail with reference to examples as means for solving the problems of the present invention, but the present invention is not limited to these examples.
［光学ガラス実施例］
先ず、表１〜表４で示す成分のガラスＮｏ．１−３５を得るために、炭酸塩、硝酸塩、硫酸塩、水酸化物、酸化物、ホウ酸等を原料とし、光学ガラス成分が対応する原料を比例によって計量して、充分に混合の後配合原料となり、当該配合原料をプラチナるつぼに入れて、１３８０〜１４５０℃まで加熱し、かつ、３〜５時間澄清撹拌後、均一な熔融ガラスとなり、更に、当該溶融ガラスを予熱した金型へ流し込み、６５０〜７００℃で２〜４時間保持後、除冷し、ガラスＮｏ．１−３５の各光学ガラス得る。
[Example of optical glass]
First, the glass numbers of the components shown in Tables 1 to 4 are shown. In order to obtain 1-35, carbonates, nitrates, sulfates, hydroxides, oxides, boric acid, etc. are used as raw materials, the raw materials corresponding to the optical glass components are weighed proportionally, and the mixture is thoroughly mixed and then blended. As a raw material, the compounded raw material is placed in a platinum crucible, heated to 1380 to 1450 ° C., and after clear stirring for 3 to 5 hours, a uniform molten glass is obtained, and the molten glass is further poured into a preheated mold. After holding at 650 to 700 ° C. for 2 to 4 hours, the glass was cooled, and the glass No. Each optical glass of 1-35 is obtained.
更に、以下に示す方法で本発明の各ガラスの特性を定義するものとし、測定結果を表１〜表４に示す。 Furthermore, the characteristics of each glass of the present invention shall be defined by the methods shown below, and the measurement results are shown in Tables 1 to 4.
（１） 屈折率ｎｄとアッベ数νｄ
屈折率とアッベ数は、ＧＢ／Ｔ ７９６２．１−２０１０によって測定する。
(1) Refractive index nd and Abbe number νd
Refractive index and Abbe number are measured by GB / T 7962.1-2010.
（２） ガラス着色度（λ７０、λ５）
相互相対の二つの光学平面を研磨した厚さ１０±０．１ｍｍのガラスサンプルで、分光透過率を測定し、その結果によって算出する。
(2) Glass coloration (λ 70 , λ 5 )
The spectral transmittance is measured with a glass sample having a thickness of 10 ± 0.1 mm obtained by polishing two mutual optical planes, and the spectral transmittance is calculated based on the result.
（３） ガラス転移温度（Ｔｇ）
ＧＢ／Ｔ７９６２．１６−２０１０規定によって測定する。
(3) Glass transition temperature (Tg)
Measured according to GB / T7962.16-2010.
（４） ガラスの密度（ρ）
ＧＢ／Ｔ７９６２．２０−２０１０規定によって測定する。
(4) Glass density (ρ)
Measured according to GB / T7692.20-2010 regulations.
（５） 化学安定性ＤＷ、ＤＡ
ＧＢ／Ｔ １７１２９の測定方法により、下記の式に基づいて算出する。
(5) chemical stability D W, D A
Calculated based on the following formula according to the measurement method of GB / T 17129.
［光学母材実施例］
表１における実施例１で得られた光学ガラスを予定の大きさにカットして、更にその表面に離型剤を均一に塗布してから、加熱・軟化の後、加圧成形して、凹面のメニスカスレンズ 、凸面のメニスカスレンズ、両凸レンズ、双凹レンズ、平凸レンズ、平凹レンズ等各種レンズ、プリズムの母材を制作する。
[Example of optical base material]
The optical glass obtained in Example 1 in Table 1 is cut to a predetermined size, a mold release agent is uniformly applied to the surface thereof, and after heating and softening, pressure molding is performed to obtain a concave surface. We manufacture various lenses such as meniscus lenses, convex meniscus lenses, biconvex lenses, biconcave lenses, plano-convex lenses, and plano-concave lenses, and prism base materials.
［光学素子実施例］
上記光学母材実施例から得られたこれらの母材をアニーリングし、ガラス内部の変形を低下すると同時に、微調整を行い、屈折率等光学特性が予期の必要値を達成させる。
[Example of optical element]
These base materials obtained from the above optical base material examples are annealed to reduce the deformation inside the glass, and at the same time, fine adjustment is performed so that the optical characteristics such as the refractive index achieve the expected required values.
次に、各母材を研削、研磨して、凹面のメニスカスレンズ、凸面のメニスカスレンズ、両凸レンズ、双凹レンズ、平凸レンズ、平凹レンズ等各種レンズ、プリズムを制作する。得られる光学素子の表面には反射防止フィルムを塗布することができる。 Next, each base material is ground and polished to produce various lenses and prisms such as a concave meniscus lens, a convex meniscus lens, a biconvex lens, a biconcave lens, a plano-convex lens, and a plano-concave lens. An antireflection film can be applied to the surface of the obtained optical element.
本発明は低コストで、且つ化学安定性の優れた高屈折低分散光学ガラスであり、屈折率は１．８５以上で、アッベ数は３５−４５で、及び記述のガラスからりなる光学素子であり、現代新型光電製品のニーズを満たすことができる。 The present invention is a high-refractive-index, low-dispersion optical glass having excellent chemical stability at low cost, having a refractive index of 1.85 or more, an Abbe number of 35-45, and an optical element made of the glass described above. Yes, it can meet the needs of modern new photoelectric products.
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| CN201510502457.7A CN106467359A (en) | 2015-08-14 | 2015-08-14 | Optical glass |
| CN201510502457.7 | 2015-08-14 | ||
| PCT/CN2016/094354 WO2017028725A1 (en) | 2015-08-14 | 2016-08-10 | Optical glass |
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| CN105198206A (en) * | 2015-08-14 | 2015-12-30 | 成都光明光电股份有限公司 | Optical glass |
| CN108726872B (en) * | 2018-07-27 | 2020-10-30 | 望江县天长光学仪器有限公司 | Optical glass |
| JP7171734B2 (en) * | 2018-08-17 | 2022-11-15 | シーディージーエム グラス カンパニー リミテッド | Optical glass, glass preform, optical element, and optical equipment having the same |
| WO2020034215A1 (en) | 2018-08-17 | 2020-02-20 | 成都光明光电股份有限公司 | Optical glass, glass preform or optical element made therefrom, and optical instrument |
| US11999651B2 (en) | 2020-09-10 | 2024-06-04 | Corning Incorporated | Silicoborate and borosilicate glasses having high refractive index and low density |
| US11976004B2 (en) | 2020-09-10 | 2024-05-07 | Corning Incorporated | Silicoborate and borosilicate glasses having high refractive index and high transmittance to blue light |
| US11802073B2 (en) | 2020-09-10 | 2023-10-31 | Corning Incorporated | Silicoborate and borosilicate glasses with high refractive index and low density |
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| JP3113604B2 (en) | 1997-03-25 | 2000-12-04 | 株式会社オハラ | Optical glass with negative anomalous dispersion |
| DE19848077C1 (en) | 1998-10-19 | 2000-01-27 | Schott Glas | Lead-free optical glass |
| JP3750984B2 (en) | 2000-05-31 | 2006-03-01 | Ｈｏｙａ株式会社 | Optical glass and optical product manufacturing method |
| DE102005020423B4 (en) | 2005-04-29 | 2009-04-02 | Schott Ag | Lead- and arsenic-free optical lanthanum borate glass and its use |
| JP5078272B2 (en) | 2006-03-31 | 2012-11-21 | 株式会社オハラ | Optical glass |
| JP5336035B2 (en) * | 2006-06-21 | 2013-11-06 | Ｈｏｙａ株式会社 | OPTICAL GLASS, GLASS MOLDED ARTICLE, OPTICAL ELEMENT AND METHOD FOR PRODUCING THEM |
| JP2010083702A (en) * | 2008-09-30 | 2010-04-15 | Hoya Corp | Optical glass, glass gob for press forming and optical element |
| CN101386469B (en) | 2008-10-16 | 2011-05-11 | 成都光明光电股份有限公司 | High refraction and low dispersion optical glass |
| JP5624832B2 (en) * | 2009-09-30 | 2014-11-12 | Hoya株式会社 | Optical glass, glass material for press molding, optical element and manufacturing method thereof |
| JP5827067B2 (en) * | 2010-08-23 | 2015-12-02 | 株式会社オハラ | Optical glass and optical element |
| CN102295409B (en) * | 2011-03-11 | 2013-12-18 | 成都光明光电股份有限公司 | Optical glass and optical element |
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| WO2013094619A1 (en) * | 2011-12-20 | 2013-06-27 | 株式会社オハラ | Optical glass and optical element |
| CN102765879A (en) * | 2012-06-25 | 2012-11-07 | 成都尤利特光电科技有限公司 | Optical glass with high refractive index and manufacturing method thereof |
| CN103241941A (en) * | 2013-05-22 | 2013-08-14 | 成都赛林斯科技实业有限公司 | Optical glass |
| CN103319086A (en) * | 2013-05-27 | 2013-09-25 | 都江堰市嘉杰光学有限责任公司 | Optical glass with high refractive index and low dispersion, and preparation method thereof |
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| CN105198206A (en) * | 2015-08-14 | 2015-12-30 | 成都光明光电股份有限公司 | Optical glass |
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